EP3505648B1 - Alliage d'aluminium haute résistance, piston de moteur à combustion interne comprenant ledit alliage et procédé de production de piston de moteur à combustion interne - Google Patents

Alliage d'aluminium haute résistance, piston de moteur à combustion interne comprenant ledit alliage et procédé de production de piston de moteur à combustion interne Download PDF

Info

Publication number
EP3505648B1
EP3505648B1 EP16915055.4A EP16915055A EP3505648B1 EP 3505648 B1 EP3505648 B1 EP 3505648B1 EP 16915055 A EP16915055 A EP 16915055A EP 3505648 B1 EP3505648 B1 EP 3505648B1
Authority
EP
European Patent Office
Prior art keywords
internal combustion
combustion engine
engine piston
comparative example
aluminum alloy
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Active
Application number
EP16915055.4A
Other languages
German (de)
English (en)
Other versions
EP3505648A1 (fr
EP3505648A4 (fr
Inventor
Izumi Yamamoto
Kazuhiro Oda
Hiroshi Horikawa
Katsumi Fukaya
Takashi Seki
Tadashi Watanabe
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Nippon Light Metal Co Ltd
Art Metal Manufacturing Co Ltd
Original Assignee
Nippon Light Metal Co Ltd
Art Metal Manufacturing Co Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Nippon Light Metal Co Ltd, Art Metal Manufacturing Co Ltd filed Critical Nippon Light Metal Co Ltd
Publication of EP3505648A1 publication Critical patent/EP3505648A1/fr
Publication of EP3505648A4 publication Critical patent/EP3505648A4/fr
Application granted granted Critical
Publication of EP3505648B1 publication Critical patent/EP3505648B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F02—COMBUSTION ENGINES; HOT-GAS OR COMBUSTION-PRODUCT ENGINE PLANTS
    • F02F—CYLINDERS, PISTONS OR CASINGS, FOR COMBUSTION ENGINES; ARRANGEMENTS OF SEALINGS IN COMBUSTION ENGINES
    • F02F3/00—Pistons 
    • F02F3/0084—Pistons  the pistons being constructed from specific materials
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent

Definitions

  • the present invention pertains to a high strength aluminum alloy, an internal combustion engine piston comprising said alloy, and a method for manufacturing an internal combustion engine piston.
  • Patent Document 1 An internal combustion engine piston of an engine of an automobile or the like is repeatedly exposed to high temperatures during use. Due thereto, strength at high temperatures and fatigue strength are demanded.
  • elements such as Si, Mg, Fe, Cu, Ni, and Mn are added to an alloy for the piston and softening at high temperatures is suppressed.
  • Patent Document 2 By refining the A1 parent phase structure, fatigue strength is improved (Patent Document 1).
  • Patent Document 3 and Patent Document 4 disclose aluminum alloys.
  • the objective of the present invention is to provide an aluminum alloy for an internal combustion engine piston that can withstand repeated use at high temperatures, and specifically, to provide an aluminum alloy having excellent heat resistance and thermal conductivity.
  • an internal combustion engine piston made of an aluminum alloy, as described in claim 3.
  • an internal combustion engine piston as described in claim 4. According to the present invention, it is possible to provide: an aluminum alloy having excellent high temperature strength and thermal conductivity; and an internal combustion engine piston comprising said alloy.
  • the aluminum alloy according to the present embodiment comprises 11.0-13.0% Si, ⁇ 0.3% Fe, 0.3-2.0% Mg, 2.0-5.0% Cu, 3.0-4.0% Ni, 0.2-1.0% Mn, 0.05-0.4% Cr, and 0.05-0.4% V, with the remainder comprising aluminum and unavoidable impurities.
  • This aluminum alloy has excellent high temperature strength and thermal conductivity.
  • Si forms eutectic Si and compounds (Mg-Si-based, Al-Si-(Mn, Cr) Fe-based, etc.) with other added elements and, in particular, improves mechanical strength at high temperatures and fatigue strength. This action is remarkable when Si content is at least 11.0%. By Si content being no more than 13%, coarsening of primary crystal Si, which is an origin of breakage, is suppressed and it is possible to suppress a decrease in mechanical strength at room temperature.
  • Fe is an unavoidable impurity incorporated from scrap, etc. which is a raw material, but forms compounds (Al-Si-(Mn, Cr) Fe-based, Al-Fe-Mn-Ni-Cr-based, etc.) with other added elements and improves strength at room temperature and high temperatures (in particular, high temperatures). Further, Fe also has an action for preventing burn-in to a metal mold.
  • Fe content being no more than 0.3%, coarsening of compounds, which is an origin of breakage, is suppressed and it is possible to suppress fatigue strength from decreasing due to mechanical properties decreasing at room temperature. Further, when Fe content is high, thermal conductivity decreases and therefore also from this perspective, limiting Fe content to no more than 0.3% is preferred. More preferably, limiting Fe content to no more than 0.2% is preferred.
  • Fe which was conventionally added with an objective of improving heat resistance strength, is one factor for a decrease in thermal conductivity and therefore the amount thereof is limited in order to increase thermal conductivity.
  • the addition amounts of Cu, Ni, and Mn are increased, the amount of formations of compounds contributing to heat resistance is increased, and solid solutions of Ti, V, and Zr are formed in the Al phase, thereby increasing heat resistance.
  • Mg forms compounds (Al-Cu-Mg-based, Mg-Si-based, etc.) with other added elements and improves strength at room temperature and high temperatures (in particular, high temperatures). This effect is remarkable when Mg is added so that Mg content is at least 0.3%. By Mg content being no more than 2.0%, it is possible to suppress a decrease in thermal conductivity.
  • Cu forms compounds (Al-Cu-based, Al-Cu-Mg-based, Al-Cu-Ni-based, etc.) with other added elements and improves strength at room temperature and high temperatures (in particular, high temperatures). This effect is remarkable when Cu content is at least 2.0%, and this effect is even more remarkable when Cu content is at least 3.0%.
  • Cu content is no more than 5.0%, coarsening of compounds, which is an origin of breakage, is suppressed and it is possible to suppress a decrease in mechanical properties (tensile strength, elongation). Due thereto, it is possible to suppress a decrease in fatigue strength and a decrease in corrosion resistance.
  • Ni forms compounds (Al-Cu-Ni-based, Al-Fe-Mn-Ni-Cr-based, etc.) with other added elements and improves strength at room temperature and high temperatures (in particular, high temperatures). This effect is remarkable when Ni is added so that Ni content is at least 3.0%. If Ni content is no more than 4.0%, coarsening of compounds, which is an origin of breakage, is suppressed and it is possible to suppress a decrease in mechanical properties at room temperature and a decrease in thermal conductivity.
  • Mn improves mechanical properties at room temperature and high temperatures. This effect is remarkable when Mn is added so that Mn content is at least 0.2%, and the effect is more remarkable when at least 0.4%. Moreover, Mn has an action of granulating Al-Si-Fe-based compounds, which readily coarsen and become acicular, as Al-Si-Mn, -Fe-based and Al-Si-(Mn, Cr)-Fe-based compounds. When an acicular crystallized product structure becomes granular, the crystallized product less readily becomes an origin of breakage, mechanical properties improve, and fatigue strength also improves.
  • Mn content being no more than 1.0%, coarsening of compounds, which is an origin of breakage, can be suppressed and it is possible to suppress fatigue strength from decreasing due to mechanical properties decreasing. It should be noted that when Mn content in the Al parent phase is large, thermal conductivity readily decreases and therefore it is preferable that the Mn content is no more than 0.5%.
  • Cr has an action of granulating Al-Si-Fe-based compounds, which readily become acicular, as Al-Si-Mn-Fe-based and Al-Si-(Mn, Cr)-Fe-based compounds.
  • an acicular crystallized product structure becomes granular, becoming an origin of breakage less readily occurs and mechanical properties improve. Fatigue strength also improves.
  • Cr also has an action of reducing the amount of Mn and Fe solid solutions in the Al parent phase and improving thermal conductivity.
  • the aluminum alloy of the abovementioned embodiment may further contain 0.05-0.4% Ti, 0.05-0.4% V, 0.05-0.4% Zr, and 0.0005-0.015% P.
  • Ti In addition to having an action of refining the Al parent phase during casting and improving elongation and fatigue strength, Ti also has an action of forming solid solutions in the Al parent phase and raising high temperature strength. This action is remarkable when Ti content is at least 0.05%. When Ti content is no more than 0.4%, it is possible to suppress coarsening of Ti compounds, which is an origin of breakage, and a decrease in mechanical properties can be suppressed. It should be noted that when the amount of Ti solid solutions in the Al parent phase is large, thermal conductivity decreases and therefore it is more preferable that Ti content is less than 0.15%.
  • V has an action of forming solid solutions in the Al parent phase and raising high temperature strength. This action is remarkable when V content is at least 0.05%.
  • V content being no more than 0.4%, the amount of solid solutions in the Al parent phase becoming large is suppressed and a decrease in thermal conductivity is suppressed. From the perspective that toughness decreases due to the suppression of creation of coarse compounds, it is more preferable that V content is less than 0.15%.
  • Zr In addition to having an action of refining the Al parent phase during casting, Zr also has an action of forming solid solutions in the Al parent phase and raising high temperature strength. This action is remarkable when Zr content is at least 0.05%, and by Zr content being no more than 0.4%, it is possible to suppress coarse Al-Zr-based compounds from crystallizing during casting and becoming a casting defect, which is an origin of breakage, and suppress mechanical properties from decreasing. It should be noted that when the amount of Zr solid solutions in the Al parent phase is large, thermal conductivity decreases and therefore it is more preferable that Zr content is less than 0.2%.
  • P has an action of refining primary crystal Si. This action is remarkable when P content is at least 0.0005%. Even if P is added so that P content exceeds 0.015%, an improvement in this action is not seen.
  • an aluminum alloy according to the abovementioned embodiment is cast and an aging treatment is performed.
  • the method for casting the alloy of the present invention is not limited to a specific method for casting, but the faster the cooling rate is during casting, the more refined the Al parent phase and the crystallized product become, and the more readily elongation and fatigue strength are improved.
  • a portion of Si, Fe, Mg, Cu, Mn, Cr, V, and Zr forms solid solutions in the Al parent phase.
  • these elements exhibit an action for inhibiting thermal conductivity.
  • the aging treatment is carried out as overaging in order to sufficiently reduce the amount of solid solutions. It should be noted that it is more preferable for a solutionizing treatment to be carried out prior to the aging treatment after casting.
  • the aluminum alloy described in the abovementioned embodiment pertains to a high strength aluminum cast alloy having excellent high temperature strength and thermal conductivity, and this alloy is particularly suitable for an internal combustion engine piston which is exposed to high temperatures.
  • An internal combustion engine piston means, specifically, a member (such as a head of a piston or the like) of a diesel piston or a gasoline piston, etc. of an automobile engine.
  • Aluminum alloys having the compositions shown in Table 1 were cast by gravity die casting (casting speed 10°C/s) in a cylindrical shape having ⁇ of 150 mm and a height of 200 mm and an aging treatment was performed with a holding temperature of 220°C and a holding time of 240 min.
  • the unit of the compositions of Table 1 is weight%.
  • Comparative Example 1 According to the results of Table 2, in Comparative Example 1, it is understood that there is a large amount of Fe and therefore tensile strength and thermal conductivity are low. Further, in Comparative Example 2, there is small amount of Ni and therefore tensile strength and fatigue strength at 350°C are low. In Comparative Example 3, there is a large amount of Ni and therefore tensile strength is low.
  • Comparative Example 4 there is a small amount of Cr and therefore thermal conductivity is low.
  • Comparative Example 5 there is a small amount of Mg and therefore tensile strength and fatigue strength at 350°C are low.
  • Comparative Example 6 there is a large amount of Mg and therefore thermal conductivity is low.
  • Comparative Example 7 there is a small amount of Si and therefore tensile strength and fatigue strength at 350°C are low.
  • Comparative Example 8 there is a large amount of Si and therefore tensile strength is low.
  • Comparative Example 9 there is a small amount of Cu and therefore tensile strength and fatigue strength at 350°C are low.
  • Comparative Example 10 there is a large amount of Cu and therefore tensile strength and thermal conductivity are low.
  • Comparative Example 11 there is a small amount of Mn and therefore tensile strength and fatigue strength are low.
  • Comparative Example 12 there is a large amount of Mn and therefore tensile strength, fatigue strength, and thermal conductivity are low.
  • Comparative Example 13 there is a large amount of Cr and therefore thermal conductivity is low.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Combustion & Propulsion (AREA)
  • General Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Pistons, Piston Rings, And Cylinders (AREA)

Claims (5)

  1. Alliage d'aluminium comprenant
    11,0-13,0 % de Si,
    ≤ 0,3 % de Fe,
    0,3-2,0 % de Mg,
    2,0-5,0 % de Cu,
    3,0-4,0 % de Ni,
    0,2-1,0 % de Mn,
    0,05-0,4 % de Cr, et
    0,05-0,4 % de V,
    avec le restant comprenant de l'aluminium et des impuretés inévitables,
    dans lequel l'alliage d'aluminium contient en outre, comme composants éventuels,
    0,05-0,4 % de Ti,
    0,05-0,4 % de Zr, et
    0,0005-0,015 % de P.
  2. Utilisation de l'alliage d'aluminium présentant la composition selon la revendication 1 pour la réalisation d'un piston de moteur à combustion interne.
  3. Piston de moteur à combustion interne fait d'un alliage d'aluminium, ledit piston comprenant un alliage d'aluminium présentant la composition selon la revendication 1 et une conductibilité thermique d'au moins 135 W/(k·m).
  4. Procédé de fabrication d'un piston de moteur à combustion interne, comprenant la coulée d'un alliage d'aluminium présentant la composition selon la revendication 1 et l'exécution d'un traitement de vieillissement, dans lequel une vitesse de coulée est dans la plage de 5-27 °C/s.
  5. Procédé de fabrication d'un piston de moteur à combustion interne selon la revendication 4, dans lequel l'alliage d'aluminium présente une conductibilité thermique d'au moins 135 W/(k·m).
EP16915055.4A 2016-08-29 2016-08-29 Alliage d'aluminium haute résistance, piston de moteur à combustion interne comprenant ledit alliage et procédé de production de piston de moteur à combustion interne Active EP3505648B1 (fr)

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
PCT/JP2016/075214 WO2018042494A1 (fr) 2016-08-29 2016-08-29 Alliage d'aluminium haute résistance, piston de moteur à combustion interne comprenant ledit alliage et procédé de production de piston de moteur à combustion interne

Publications (3)

Publication Number Publication Date
EP3505648A1 EP3505648A1 (fr) 2019-07-03
EP3505648A4 EP3505648A4 (fr) 2020-03-04
EP3505648B1 true EP3505648B1 (fr) 2021-03-24

Family

ID=61300267

Family Applications (1)

Application Number Title Priority Date Filing Date
EP16915055.4A Active EP3505648B1 (fr) 2016-08-29 2016-08-29 Alliage d'aluminium haute résistance, piston de moteur à combustion interne comprenant ledit alliage et procédé de production de piston de moteur à combustion interne

Country Status (5)

Country Link
US (1) US11549461B2 (fr)
EP (1) EP3505648B1 (fr)
JP (1) JP6743155B2 (fr)
CN (1) CN109642275B (fr)
WO (1) WO2018042494A1 (fr)

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN111020303A (zh) * 2019-11-27 2020-04-17 亚太轻合金(南通)科技有限公司 4xxx系铝合金及其制备方法
CN111394628B (zh) * 2020-05-15 2021-06-04 浙大宁波理工学院 一种原位双相颗粒增强富Fe活塞铝基复合材料及其制备方法
CN111455233B (zh) * 2020-05-27 2021-11-26 东莞市青鸟金属材料有限公司 一种高导热铝合金材料及其制备方法
EP4373985A1 (fr) * 2021-07-23 2024-05-29 Tesla, Inc. Alliages d'aluminium pour coulée brasable

Family Cites Families (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4975243A (en) * 1989-02-13 1990-12-04 Aluminum Company Of America Aluminum alloy suitable for pistons
US5162065A (en) * 1989-02-13 1992-11-10 Aluminum Company Of America Aluminum alloy suitable for pistons
US5055255A (en) * 1989-02-13 1991-10-08 Aluminum Company Of America Aluminum alloy suitable for pistons
JP3878069B2 (ja) * 2002-06-27 2007-02-07 日本軽金属株式会社 高温強度に優れたアルミニウム合金およびその製造方法
JP4075523B2 (ja) 2002-08-20 2008-04-16 株式会社豊田中央研究所 ピストン用アルミニウム鋳造合金，ピストン及びその製造方法
JP2004256873A (ja) 2003-02-26 2004-09-16 Nippon Light Metal Co Ltd 高温強度に優れた鋳物用アルミニウム合金
JP4707413B2 (ja) * 2005-03-04 2011-06-22 三菱樹脂株式会社 連続鋳造アルミニウム合金鋳塊及びその製造方法
CN101522935B (zh) 2006-08-01 2012-09-26 昭和电工株式会社 铝合金成形品的制造方法、铝合金成形品以及生产系统
JP5300118B2 (ja) * 2007-07-06 2013-09-25 日産自動車株式会社 アルミニウム合金鋳物の製造方法
JP5449754B2 (ja) * 2008-12-08 2014-03-19 宮本工業株式会社 エンジンまたはコンプレッサーのピストンの鍛造方法
CN103003458B (zh) * 2010-07-16 2015-11-25 日本轻金属株式会社 高温强度和导热率优良的铝合金及其制造方法
JP2014152375A (ja) * 2013-02-13 2014-08-25 Art Metal Mfg Co Ltd 内燃機関用ピストン材料及びその製造方法
US9834828B2 (en) * 2014-04-30 2017-12-05 GM Global Technology Operations LLC Cast aluminum alloy components
DE102016213352A1 (de) * 2016-07-21 2018-01-25 Federal-Mogul Wiesbaden Gmbh Bleifreies Aluminiumgleitlagermaterial mit Funktionsoberfläche

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
None *

Also Published As

Publication number Publication date
EP3505648A1 (fr) 2019-07-03
CN109642275A (zh) 2019-04-16
US11549461B2 (en) 2023-01-10
WO2018042494A1 (fr) 2018-03-08
US20190186410A1 (en) 2019-06-20
JP6743155B2 (ja) 2020-08-19
CN109642275B (zh) 2023-10-20
JPWO2018042494A1 (ja) 2019-03-14
EP3505648A4 (fr) 2020-03-04

Similar Documents

Publication Publication Date Title
JP5582532B2 (ja) Ｃｏ基合金
JP4277113B2 (ja) 耐熱ばね用Ｎｉ基合金
EP3505648B1 (fr) Alliage d'aluminium haute résistance, piston de moteur à combustion interne comprenant ledit alliage et procédé de production de piston de moteur à combustion interne
JP6491452B2 (ja) アルミニウム合金連続鋳造材及びその製造方法
WO2017033663A1 (fr) Matériau extrudé en alliage d'aluminium et un procédé pour sa production
JP2013142168A (ja) 耐クリープ特性に優れたアルミニウム合金
CN109023183B (zh) 一种稀土镁合金铸锭热处理工艺
JP2010018854A (ja) 耐熱性に優れた軽量・高強度アルミニウム合金およびその製造方法
JP2011122180A (ja) 高温強度及び高温疲労特性に優れた耐熱アルミニウム合金押出材
JP2019108579A (ja) アルミニウム合金材およびアルミニウム合金製品の製造方法
JP2004176162A (ja) 銅合金およびその製造方法
JP6587533B2 (ja) 疲労強度特性に優れた切削加工用アルミニウム合金押出材及びその製造方法
EP3480326A1 (fr) Feuille en alliage d'aluminium présentant une excellente résistance à la formation de stries et une excellente aptitude au pliage de du bord rabattu et procédé pour sa production
JP4771791B2 (ja) 成形加工用アルミニウム合金板の製造方法
JP6015536B2 (ja) 冷間塑性加工用熱処理型アルミニウム合金及びその製造方法
KR101797131B1 (ko) 주조용 마그네슘 합금 및 이의 제조방법
JP2007239005A (ja) 室温非時効性、成形性及び塗装焼付け硬化性に優れた６０００系アルミニウム合金板の製造方法
JP2020169378A (ja) コンプレッサー摺動部品用アルミニウム合金およびコンプレッサー摺動部品鍛造品
JP7126915B2 (ja) アルミニウム合金押出材及びその製造方法
KR101846735B1 (ko) 실린더 헤드용 알루미늄 합금 및 이의 제조방법
JP2005281742A (ja) アルミニウム合金、該アルミニウム合金からなる流体機器のスクロール部およびその製造方法。
KR101856381B1 (ko) 실린더 헤드용 알루미늄 합금
JP6512963B2 (ja) 室温時効を抑制し、かつ、焼付硬化性に優れたアルミニウム合金板
CN115961192A (zh) 锶锆钛铒铈五元复合微合金化的800MPa强度级高性能铝合金及其制备方法
KR101787550B1 (ko) 마그네슘 합금 및 이의 제조방법

Legal Events

Date Code Title Description
STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE INTERNATIONAL PUBLICATION HAS BEEN MADE

PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: REQUEST FOR EXAMINATION WAS MADE

17P Request for examination filed

Effective date: 20190315

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

AX Request for extension of the european patent

Extension state: BA ME

DAV Request for validation of the european patent (deleted)
DAX Request for extension of the european patent (deleted)
A4 Supplementary search report drawn up and despatched

Effective date: 20200204

RIC1 Information provided on ipc code assigned before grant

Ipc: C22F 1/043 20060101ALI20200129BHEP

Ipc: F02F 3/00 20060101ALI20200129BHEP

Ipc: C22C 21/02 20060101AFI20200129BHEP

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: GRANT OF PATENT IS INTENDED

RIN1 Information on inventor provided before grant (corrected)

Inventor name: WATANABE TADASHI

Inventor name: ODA KAZUHIRO

Inventor name: HORIKAWA HIROSHI

Inventor name: FUKAYA KATSUMI

Inventor name: SEKI TAKASHI

Inventor name: YAMAMOTO IZUMI

INTG Intention to grant announced

Effective date: 20201112

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE PATENT HAS BEEN GRANTED

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 1374587

Country of ref document: AT

Kind code of ref document: T

Effective date: 20210415

Ref country code: DE

Ref legal event code: R096

Ref document number: 602016055059

Country of ref document: DE

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG9D

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: HR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210324

Ref country code: FI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210324

Ref country code: NO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210624

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210624

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LV

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210324

Ref country code: RS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210324

Ref country code: SE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210324

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20210324

REG Reference to a national code

Ref country code: AT

Ref legal event code: MK05

Ref document number: 1374587

Country of ref document: AT

Kind code of ref document: T

Effective date: 20210324

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: NL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210324

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210324

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210324

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210324

Ref country code: AT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210324

Ref country code: SM

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210324

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210724

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210324

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210324

Ref country code: PL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210324

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210726

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602016055059

Country of ref document: DE

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210324

Ref country code: AL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210324

Ref country code: ES

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210324

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210324

26N No opposition filed

Effective date: 20220104

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210324

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20210831

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210831

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210831

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210724

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210829

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210829

Ref country code: BE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210831

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210324

P01 Opt-out of the competence of the unified patent court (upc) registered

Effective date: 20230516

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210324

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: HU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO

Effective date: 20160829

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210324

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: GB

Payment date: 20230822

Year of fee payment: 8

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FR

Payment date: 20230828

Year of fee payment: 8

Ref country code: DE

Payment date: 20230821

Year of fee payment: 8

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210324

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210324